Microstructure and Hardness Evolution in Magnesium Processed by HPT

Abstract

High pressure torsion provides an opportunity to process materials with low formability such as magnesium at room temperature. The present work shows the microstructure evolution in commercially pure magnesium processed using a pressure of 6.0 GPa up to 10 turns of rotation. The microstructure evolution is evaluated using electron microscopy and the hardness is determined using dynamic hardness testing. The results show that the grain refinement mechanism in this material differs from materials with b.c.c. and f.c.c. structures. The mechanism of grain refinement observed at high temperatures also applies at room temperature. The hardness distribution is heterogeneous along the longitudinal section of the discs and is not affected by the amount of deformation imposed to the material.

Keywords:
high-pressure torsion; magnesium; EBSD

1. Introduction

High-pressure torsion (HPT)^1,2 is a metal processing technique in which a sample is subjected to torsion under elevated pressure. The pressure leads to high hydrostatic compressive stresses and severe plastic deformation is introduced by torsion increasing significantly the amount of crystalline defects in the material structure. Thus, a high dislocation density and an increased area of grain boundaries are observed in processed metallic materials leading to high strength and refined grain structures.

High pressure torsion has been widely used to process magnesium and its alloys at room temperature despite their low formability. Many papers have reported the formation of ultrafine grained structures in pure magnesium^3-6 and AZ31^7-11, AZ61¹², AZ80¹³, AZ91^14-16, ZK60^17-19, Mg-Zn-Y^20,21, Mg-Gd-Y-Zr^22,23, Mg-Zn-Ca^24-27 and Mg-Dy-Al-Zn-Zr²⁸ alloys. The processed alloys exhibit improved strength but also some papers report superplastic behaviour^{16,19,22,29,30}, improved hydrogen storage properties^3,31-35 and improved corrosion resistance^24,27,36.

Formation of ultrafine grained structures and improved strength are also observed in other metallic materials processed by HPT. However, the evolution of the microstructure and the distribution of hardness in processed discs of magnesium and its alloys seem to differ from other f.c.c. and b.c.c. materials. It is expected that the amount of strain imposed to the disc during HPT processing is proportional to the distance from the center due to the torsional deformation. Thus, hardness variations along the sample radius are expected in the early stage of processing when the material has not reached hardness saturation. However, the amount of strain and the hardness are not expected to vary along the sample thickness and this has been confirmed by experiments in pure aluminium^37,38 and iron³⁹. Minor variations in distribution of strain along the sample thickness has been predicted by finite element modelling^40,41 due to friction and variations in hardness distribution have been reported in samples with low diameter to thickness ratio^39,42. However, experiments have shown significant heterogeneity in hardness distribution along the disc thickness in a magnesium alloy in samples with high diameter to thickness ratio^43,44.

Moreover, it is known that the high amount of defects introduced by plastic deformation leads to the formation of low angle boundaries in the early stage of processing and the misorientation of these boundaries increase with continuing processing. Therefore, a large fraction of low angle boundaries are expected in the early stage of HPT processing and a gradual transition towards a larger fraction of high angle boundaries is expected at later stages. This has been confirmed by experiments in aluminium^45,46 and in pure iron⁴⁷. However, the mechanism of grain refinement in magnesium and its alloys differs from f.c.c. and b.c.c. materials. A mechanism in which new refined grains are formed along coarse grains boundaries has been proposed^48-50 based on experimental evidence of microstructure evolution for high temperature processing.

The understanding of the distribution of plastic deformation and evolution of structure during HPT processing is of key importance to future production of components of magnesium alloys with superior strength, superplastic properties, enhanced hydrogen storage kinetics or improved corrosion resistance. The present paper aims to clarify the distribution of hardness along the disc longitudinal plane using dynamic hardness measurements at different stages of HPT processing and to determine the evolution of grain boundary misorientation distribution.

2. Experimental Material and Procedures

The material used in the present work was commercial purity magnesium provided by RIMA (Bocaiúva / Brazil) as a cast slab. The material was machined into a billet with 10 mm diameter and 100 mm length. Discs with 1 mm thickness were cut using a low speed diamond coated saw and were ground to ~0.85 mm thickness using abrasive papers.

The discs were processed by HPT using quasi-constrained anvils and a nominal pressure of 6.0 GPa. The rotation rate was 1 rpm which is expected to lead to ~10 K temperature rise during processing (considering a flow stress of 200 MPa)^51,52. Discs were processed to 1/8, 1/2, 2 and 10 turns.

The distribution of hardness was determined on the longitudinal section of the discs. A low speed diamond coated saw was used to cut the discs and the samples were mounted using room temperature curing resin. The samples were ground and polished to a mirror-like finish. Figure 1 illustrates the section and the location of indentations. A Shimadzu DUH-211s dynamic hardness tester with a Berkovich indenter was used for testing. The maximum applied load was 200 mN, the loading rate was ~70 mN/s and the dwell time was set to 0 s in order to avoid room temperature creep which has been shown to take place in magnesium processed by HPT⁶. The values of hardness were plotted as colour coded maps as a function of the indentation position. Also, the average hardness for indentations at similar distance from the center were plotted as a function of the effective strain which was determined by the following equation^53,54.

Figure 1
Illustration of the section used for hardness testing, location of indentations and the location for EBSD characterization of the microstructure.

(1) $\varepsilon =\frac{2\pi \mathit{Nr}}{\mathit{t}\surd 3}$

where N is the number of turns, r is the distance to the center and t is the sample thickness.

The microstructure was determined at mid-radius position (see Figure 1) using EBSD. The samples were polished to a mirror-like finish using diamond paste and the final polishing step used colloidal silica in a Vibromet equipment. The equipment used for EBSD characterization was a JEOL JSM-7001F scanning electron microscope operating at 7 kV. The step size was 0.1 µm. The images were cleaned up using grain confidence index (CI) standardization, neighbor CI correlation and grain dilation procedures.

3. Results and Discussion

3.1 Microstructure

Figure 2 shows representative images of the grain structure of samples processed by 1/8, 1/2 and 10 turns of HPT. Different colours are used to set apart low angle (red) and high angle (black) boundaries. Grains sizes with over one order of magnitude difference are clearly observed in the sample processed by 1/8 turn. The smaller grains are typically located between coarse grains suggesting they are formed along grain boundaries. The microstructure of the material processed by 1/2 turn exhibits grains with different sizes although the size difference between the small and coarse grains is reduced significantly. Also, the area fraction occupied by the coarse grains decreased significantly by comparison to the material processed by 1/8 turn. Finally, the microstructure of the material processed by 10 turns of HPT continues to exhibit a few coarse grains although it is apparent that the area fraction of the coarse grains is reduced. This is in agreement with transmission electron microscopy characterization of magnesium processed by HPT in which some coarser grains are observed in the microstructure even after multiple turns of processing^3,6,55. Therefore, a mix of ultrafine grains and grains with a few microns of diameter seems to be a stable microstructure in pure magnesium processed by HPT.

Figure 2
Distribution of low angle (red) and high angle (black) boundaries in samples processed by 1/8, 1/2 and 10 turns of HPT.

In order to determine the area fraction occupied by coarse and fine grains at the different stages of processing, the cumulative distribution of grain sizes in samples processed by 1/8, 1/2 and 10 turns of HPT is shown in Figure 3. It is observed that most of the microstructure is composed of grains larger than 1 micron in the sample processed by 1/8 turn. Processing to 1/2 turn increases significantly the area occupied by ultrafine grains and decreases the size of the largest grains. Further processing up to 10 turns does not change the distribution of the very fine grains (<0.6 µm) but increased the fraction of grains in the range 0.6 µm ~ 1.0 µm and reduced the fraction of coarser grains. This is in agreement with the trend observed in magnesium processed by Equal-Channel Angular Pressing at high temperatures in which the new grains nucleate along grain boundaries and slowly consume the coarse grains ^48-50.

Figure 3
Cumulative fraction of grain sizes at different stages of processing.

Figure 4 shows the distribution of misorientation angles of the grain boundaries for the different samples. A large fraction (~0.41) of grain boundaries exhibit misorientations lower than 15º after only 1/8 turn but the frequency of low angle boundaries is decreased significantly after only 1/2 turn (~0.27). An additional decrease in frequency of low angle boundaries is observed after 10 turns which ultimately stabilizes in ~0.15. The frequency of low angle boundaries in magnesium is significantly lower than observed in other metallic materials^46,47. It is also worth noting a peak of frequency of boundaries between 85º ~ 90º which is associated with twinning⁵⁶ and a peak at ~30º which is associated with a basal texture⁵⁷.

Figure 4
Frequency distribution of misorientation angles of grain boundaries.

3.2 Hardness

Figure 5 shows colour-coded distribution of hardness at the longitudinal sections of samples processed to 1/8, 1/2, 2 and 10 turns of HPT. It is observed that the hardness does not vary notably with the distance from the center and also does not vary with the number of turns although the amount of plastic strain imposed to the material by torsion increases linearly with increasing distance from the center and with the number of turns. The hardness maps show substantial variations in hardness without a clear trend. Areas with low hardness (~50 kgf mm^-2) and areas with high hardness (~65 kgf mm^-2) are observed throughout the longitudinal sections of the samples at the different stages of processing. This heterogeneous distribution of hardness differs from reports in pure aluminum³⁸ and in pure iron ³⁹ where homogeneous distributions of hardness have been reported along the sample thickness and a clear trend is observed at different distances from the center.

Figure 5
Distribution of hardness at the longitudinal section of discs processed by HPT to 1/8, 1/2, 2 and 10 turns.

Figure 6 shows the average hardness plotted as a function of the effective strain. It is observed that the hardness does not vary significantly with the amount of effective strain. Hardness values in the range 55 ~ 60 kgf mm² are observed at strains in the range 0.3 ~ 200. This disagrees with a report in the literature of a peak hardness at low strains followed by slight softening and saturation³. The softening observed at intermediate values of strain in pure magnesium is usually attributed to the occurrence of recovery and recrystallization in this material³. However, the present results show that this may not be the case since softening was not observed in the present experiments. Recent reports have shown that pure magnesium exhibits an inverse Hall-Petch relation at very small grain sizes ⁵⁸ and a change in deformation mechanism^6,58 takes place at levels of strain in which the softening effect is usually observed. Grain boundary sliding starts to play a role in deformation leading to an apparent softening effect. Thus, the decrease in hardness is attributed to creep by grain boundary sliding during dwell time in conventional hardness testing. The indentations in the present work were controlled and the dwell time was removed in order to prevent creep and therefore the softening effect was not observed.

Figure 6
Distribution of hardness as a function of the imposed effective strain in HPT.

4. Summary and Conclusions

1. High-pressure torsion was used to introduce severe plastic deformation in pure magnesium. EBSD characterization revealed the formation of small grains along grain boundaries of coarse grains. The fine grains gradually consume the coarse grains with increasing imposed strain.

2. The gradual increase in fraction of ultrafine grains and the fast evolution of the distribution of grain boundary misorientation towards high angles differs from other metallic materials and agrees with a model of grain refinement for magnesium processed at high temperatures.

3. The distribution of hardness is heterogeneous along the longitudinal plane of the processed disc which also differs from other metallic materials.

4. The average hardness does not vary with the amount of imposed effective strain during HPT. The softening effect reported in the literature is attributed to the onset of grain boundary sliding and creep during dwell time in conventional hardness testing.

5. Acknowledgements

The authors acknowledge support from CNPq, FAPEMIG and CAPES. One of the authors acknowledges support from the European Research Council under ERC Grant Agreement No. 267464-SPDMETALS (TGL).

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Publication Dates

• Publication in this collection
  12 Sept 2017
• Date of issue
  2017

History

• Received
  23 Feb 2017
• Accepted
  27 July 2017